EP0389096A1 - Verfahren zum bereichsweisen Frischen von orientiertem Siliciumstahl - Google Patents

Verfahren zum bereichsweisen Frischen von orientiertem Siliciumstahl Download PDF

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Publication number
EP0389096A1
EP0389096A1 EP90301541A EP90301541A EP0389096A1 EP 0389096 A1 EP0389096 A1 EP 0389096A1 EP 90301541 A EP90301541 A EP 90301541A EP 90301541 A EP90301541 A EP 90301541A EP 0389096 A1 EP0389096 A1 EP 0389096A1
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Prior art keywords
steel
agent
flux
heating
base coating
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EP90301541A
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English (en)
French (fr)
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Stuart Leslie Ames
Charles Dean Boyer
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Allegheny Ludlum Corp
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Allegheny Ludlum Corp
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1294—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a localized treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H01F1/14766—Fe-Si based alloys
    • H01F1/14775—Fe-Si based alloys in the form of sheets
    • H01F1/14783—Fe-Si based alloys in the form of sheets with insulating coating

Definitions

  • This invention relates to a method of improving core loss of grain oriented silicon steel by refining magnetic domain wall spacing. More particularly, the invention relates to a method of processing final texture annealed steel by applying an agent selectively to remove the oxide base coating before thermally and/or chemically treating to effect heat resistant domain refinement.
  • Grain-oriented silicon steel is conventionally used in electrical applications, such as power transformers, distribution transformers, generators, and the like.
  • the steel's ability to permit cyclic reversals of the applied magnetic field with only limited energy loss is a most important property. Reductions of this loss, which is termed "core loss”, is desirable.
  • the Goss secondary recrystallization texture (110)[001] in terms of Miller,s indices, results in improved magnetic properties, particularly permeability and core loss over nonoriented silicon steels.
  • the Goss texture refers to the body-centered cubic lattice comprising the grain or crystal being oriented in the cube-on-edge position.
  • the texture or grain orientation of this type has a cube edge parallel to the rolling direction and in the plane of rolling, with the (110) plane being in the sheet plane.
  • steels having this orientation are characterized by a relatively high permeability in the rolling direction and a relatively low permeability in a direction at right angles thereto.
  • typical steps include providing a melt having of the order of 2-4.5% silicon, casting the melt, hot rolling, cold rolling the steel to final gauge typically of 7 or 9 mils (0.1778 or 0.2286mm), and up to 14 mils (0.3556mm) with an intermediate annealing when two or more cold rollings, are used, decarburizing the steel, applying a refractory oxide base coating, such as a magnesium oxide coating, to the steel, and final texture annealing the steel at elevated temperatures in order to produce the desired secondary recrystallization and purification treatment to remove impurities such as nitrogen and sulfur.
  • the development of the cube-on-edge orientation is dependent upon the mechanism of secondary recrystallization wherein during recrystallization, secondary cube-on-edge oriented grains are preferentially grown at the expense of primary grains having a different and undesirable orientation.
  • the final texture annealed grain oriented silicon steel sheet has an insulation coating thereon resulting from an annealing separator coating, i.e. refractory oxide base coating, applied before the texture anneal to stop the laps of the coil from thermally welding or sticking together during the high temperature anneal and to promote formation of an oxide film on the steel surface.
  • This film is desirable because it is an electrical insulator and can form part, or sometimes all, of the insulation needed when the steel is in operation in a transformer.
  • Such an insulative oxide coating forming naturally during the texture anneal is known variously as forsterite, the base coating, or mill glass.
  • sheet and “strip” are used interchangeably and mean the same unless otherwise specified.
  • first, regular or conventional grain-oriented silicon steel, and second, high permeability grain-oriented silicon steel are generally characterized by permeabilities of less than 1850 at 10 Oersteds with a core loss of greater than 0.400 watts per pound (WPP) (0.882 watts per kilogram (WKg) at 1.5 Tesla at 60 Hertz for nominally 90mil (02286 mm) material.
  • WPP watts per pound
  • WKg 0.882 watts per kilogram
  • High permeability grain-oriented silicon steels are characterized by higher permeabilities which may be the result of compositional changes alone or together with process changes.
  • high permeability silicon steels may contain nitrides, sulfides, and/or borides which contribute to the precipitates and inclusions of the inhibition system which contributes to the properties of the final steel product.
  • high permeability silicon steels generally undergo heavier cold rolling reduction to final gauge than regular grain oriented steels for a final heavy cold reduction of the order of greater than 80% is made in order to facilitate the high permeability grain orientation. While such higher permeability materials are desirable, such materials tend to produce larger magnetic domains than conventional material. Larger domains are deleterious to core loss.
  • domain size and thereby core loss values of electrical steels may be reduced is if the steel is subjected to any of various practices designed to induce localized strains in the surface of the steel.
  • Such practices may be generally referred to as "domain refining by scribing" and are performed after the final high temperature annealing operation. If the steel is scribed after the final texture annealing, then there is induced a localized stress state in the texture-annealed sheet so that the domain wall spacing is reduced.
  • These disturbances typically are relatively narrow, straight lines, or scribes, generally spaced at regular intervals. The scribe lines are substantially transverse to the rolling direction and typically are applied to only one side of the steel. See U.S. Patents 3,647,575 issued March 7, 1972: 4,513,597 issued April 30, 1985, and 4,680,062 issued July 14, 1987.
  • the method includes imparting a strain to the sheet, forming an intruder on the grain-oriented sheet, the intruder being of a different component or structure than the electrical sheet and doing so either prior to or after straining and thereafter annealing such as in a hydrogen reducing atmosphere to result in imparting the intruders into the steel body.
  • Numerous metals and nonmetals are identified as suitable intruder materials.
  • Japanese Patent Document 61-133321A discloses removing surface coatings from final texture annealed magnetic steel sheet, forming permeable material coating on the sheet and heat treating to form material having components or structure different than those of the steel matrix at intervals which provide heat resistant domain refinement.
  • Japanese Patent Document 61-139,679A discloses a process of coating final texture annealed oriented magnetic steel sheet in the form of linear or spot shapes, at intervals with at least one compound selected from the group of phosphoric acid, phosphates, boric acid, borates, sulfates, nitrates, and silicates, and thereafter baking at 300-1200°C, and forming a penetrated body different from that of the steel to refine the magnetic domains.
  • Japanese Patent Document 61 284529A discloses a method of removing the surface coatings from final texture annealed magnetic steel sheets at intervals, coating one or more of zinc, zinc alloys, and zincated alloy at specific coating weights, coating with one or more of metals having a lower vapor pressure than zinc, forming impregnated bodies different from the steel in composition or in structure at intervals by heat treatment or insulating film coating treatment to refine the magnetic domains.
  • Japanese Patent Document 62-51202 discloses a process for improving the core loss of silicon steel by removing the forsterite film formed after final texture annealing, and adhering different metal, such as copper, nickel, antimony by heating.
  • What is needed is a convenient and inexpensive method for removing the base coating in desired patterns in a method of refining the magnetic domain wall spacing of grain-oriented silicon steel.
  • the method should be compatible with conventional processing of regular and high permeability silicon steels, should make use of the thermally insulative coating on the sheet, and should be useful with numerous subsequent techniques to facilitate the domain refinement.
  • the present invention provides a method of refining the magnetic domain wall spacing of grain-oriented final texture annealed silicon steel sheet having an insulation base coating thereon, the method being as defined in claim 1.
  • a method of refining the magnetic domain wall spacing of grain-oriented final texture annealed silicon steel having an insulation coating thereon comprises removing portions of the oxide base coating to substantially expose a predetermined line pattern of the underlying steel.
  • the removal may include applying, preferably by printing, a fluxing agent to the base coated steel in the line pattern, and then heating the agent on the steel to react and cause substantial removal of the base coating in the line pattern with little or no surface damage to the steel.
  • Heat resistant domain refinement and reduced core loss is effected by allowing further chemical and/or thermal treatment activity on the substantially exposed steel areas.
  • the method of the present invention relates to a particular process of removing preselected portions of the oxide coating of silicon steel for thereafter effecting heat resistant domain refinement by allowing thermal and/or chemical treatment of the exposed steel, by any of several subsequent techniques.
  • the width, spacing and pattern of lines of removed base coating may take the form of any of several conventional or known scribe patterns, preferably lines substantially transverse to the rolling direction.
  • the pattern is uniquely removed by applying, preferably by printing, an agent e.g., a fluxing agent, to the oxide base coated steel in the desired pattern and heating the agent to react and cause substantial removal of the base coating in the pattern with little or no surface damage to the steel, and possibly with no immediate improvement, and maybe even a deterioration, of magnetic properties.
  • Heat resistant domain refinement and reduced core loss are thereafter effected by allowing thermal and/or chemical treatment on the pattern of exposed steel.
  • the invention is particularly useful in conventional processing lines wherein steel strip moves at speeds of up to 500 feet (152m) per minute.
  • the invention should also be useful at higher speeds of up to 2000 feet (610m) per minute such as used in high speed printing techniques. It appears that the constraint on speed primarily may depend on the time for the "ink” to dry.
  • High speed "firing" devices such as induction or radiant heaters which heat surface layers should be useful.
  • the method includes applying, preferably by printing, a flux agent to the base coated steel in a desired pattern. It has been found that conventional printing techniques and equipment may be suitable if modified so as to apply a suitable agent to the silicon steel at desired speeds, thicknesses and patterns.
  • FIG. 1 Two methods and equipment of continuous printing are shown schematically in Figures 1 and 2.
  • Figure 1 is a schematic of a widely used conventional offset printing press in which a cluster of three rolls are used in applying the ink.
  • the ink roll 1 rotates about its axis, dips into ink well 2, collects a layer of ink which is metered or wiped to a uniform layer as it passes against metering bar 3.
  • the inked roll 1 then presses against the rotating second roll, i.e. print roll 4 on which the print, pattern, or design (hereinafter print-message) is located.
  • the inked print roll 4 then presses against rotating third roll 5, the so-called blanket roll, on to which the print-message is transferred from roll 4.
  • the rotating blanket roll presses against the substrate strip 6 and the print message is transferred to the strip 6 as it moves continuously between roll 5 and backup roll 7.
  • the back-up roll 7 may or may not be necessary with this invention although it is conventionally used in the paper industry.
  • FIG 2 a schematic of known flexographic printing is illustrated.
  • the process is a modification of conventional three-roll offset printing, with the important difference being that new materials which are both tough and flexible are used for the print roll 4A.
  • new materials may be special rubbers or photo-polymers. They are sufficiently rugged for making direct contact with and printing on the moving substrate rather than via a blanket roll.
  • the ink delivery roll 1 for offset printing of Figure 1 is conventionally solid and smooth
  • the flexographic printer of Figure 2 has a honeycombed surface of ink roll 1A against which the flexible print roll 4A presses, literally sucking the ink out of the honeycomb cells.
  • the back-up roll 7A included in Figure 2 is conventional but may not be essential for strong substrates such as metal.
  • stencilling methods can be used (not shown).
  • the substrate to be printed is covered with a mask which has the print-­message precut through as slots and openings.
  • Ink is rolled or sprayed onto the stencil-substrate assembly and contacts the substrate in the slotted areas. Removal of the stencil completes the printing operation and reveals the printed substrate.
  • the consistency and viscosity of the ink used in printing techniques may vary and is dependent on the technique used.
  • the ink used for offset printing has to be of similar viscosity to thick syrup (e.g. 10,000 centipoise (10 Pa.s)).
  • Flexographic printing is much more tolerant of ink viscosity and is capable of printing inks from thin liquid to paste consistencies.
  • stencilling the ink has to have a thick consistency for roller application, and must have a thin consistency for spray application.
  • Grain-oriented silicon steel used in the herein disclosed tests was produced by casting, hot rolling, normalizing, cold rolling to intermediate gauge, annealing and cold rolling to final gauge, decarburizing, and final texture annealing to achieve the desired secondary recrystallization of cube-on-edge orientation.
  • Typical melts of nominal initial composition of conventional (Steel 1) and high permeability (Steel 2) grain-­oriented silicon steels were: ELEMENTS C N Mn S Si Cu B Fe Steel 1 030 ⁇ 50ppm .07 .022 3.15 .22 - Bal Steel 2 030 ⁇ 50ppm .038 .017 3.15 .30 10ppm Bal After final texture annealing, the C, N, and S were reduced to trace levels of less than about 0.001%. The strip was cut into numerous pieces to produce samples of sizes sufficient for processing in accordance with the present invention. Final sample size for magnetic testing was that of the well known Epstein strip of 30cm. long x 3 cm. wide. Epstein strips were tested both as stacked packs and as single strips as indicated.
  • the method of the present invention recognizes that the layer of forsterite required to be broken through or substantially removed is very thin, typically 5 microns (.005mm). It has been found that the layer can be penetrated easily and quickly, using a small amount of a fluxing agent.
  • the flux agent is applied to the forsterite surface in the precise pattern of lines needed for a subsequent chemical and/or thermal treatment to develop heat-proof domain refinement.
  • the pattern of exposed or substantially exposed pattern of lines through the forsterite to the silicon steel substrate is referred to as "metal stripes”.
  • the flux agent may be applied or printed in various thicknesses to the base coating depending on flux agent consistency, concentration, heating time and temperatures.
  • the thickness may range from 0.005 to 0.127mm (0.02 to 0.5 mils).
  • a suitable flux agent should have a consistency and viscosity compatible with the method of application or printing to the silicon steel.
  • the agent must be capable of dissolving the oxide layer, i.e. forsterite, formed on the final texture annealed steel.
  • the agent should be capable of being self-activated or activated in a manner consistent with manufacturing processes for grain oriented silicon steel. A relatively low temperature heating step must be used.
  • a fluxing agent for dissolving the oxide layer formed on the steel as used in brazing can include: Boric Acid, Borates, Chlorides, Fluorides, Fluoroborates, and Phosphoric Acid. While only the salt radical is listed above, the metal radical is frequently from the group of sodium, potassium and lithium. It was found that one of many commercial fluxes employed commonly for brazing and soldering steels may be suitable. There are several generic fluxes available from this group which are effective at firing temperatures in air between approximately 1050°F and 1600°F (566 and 871°C), and are available as powder, paste, or liquid. There are also available proprietary brand fluxes, such as sold under the tradenames "Stay-Silv", “Brazo-Flux" and "Welco-Flux".
  • the applied flux agent must be subject to heat to effect the firing or activation in which connection the invention contemplates the employment of a heating zone immediately following the printing step.
  • the application of the "heating" or “firing” step can be performed in a furnace at a temperature of greater than 200°F (93°C) and preferably 900°F-1650°F (482-899°C) and more preferably 1050°F-1600°F (566 to 871°C).
  • the heating is a rapid heating with no substantial hold time.
  • the fluxing action is intensified when firing is in air.
  • a reducing atmosphere such as hydrogen or an inert atmosphere, such as argon, completely inhibits the reaction and cannot be used.
  • the method of the invention requires a substantially oxidizing atmosphere, such as an air atmosphere.
  • the stencil was a thin plastic sheet of a size suitable for covering an Epstein strip and had 0.5mm wide slits cut out forming parallel openings at 5mm intervals.
  • the flux paste was first applied as a thin layer to a dummy metal strip.
  • the stencil was then interposed between the pasted dummy strip and the test strip of silicon steel.
  • the sandwich so formed was subjected to gentle pressure by a roller sufficient to apply the flux on the test strip in a line pattern generally transverse to the rolling direction of the test strip.
  • the stencil was then peeled from the sandwich.
  • Figure 3A and 3B are representative photomicrographs, 30X and 100X respectively, of the surface of a 7 mil (0.1778mm) test specimen after printing and heating to show craters or breaks through the base glass. Using the previously described copper sulfate test as indicative of breakthrough of the forsterite, all samples showed adequate breakthrough.
  • phosphorus migrates to any exposed iron (such as the metal stripes), attacks the iron, and forms wedge-­shaped phosphide particles.
  • phosphorus was applied as described in the application by roller coating of a "P" coating having the following solution Phosphoric Acid 118 gm/1 Magnesium Oxide 18 gm/1 Ammonium Hydroxide (58%) 20 gm/1 Chromium Dioxide 34 gm/1 Tonol (2%) 1 gm/1 Water Balance
  • the coated metal strip samples were air dried for 1 minute at 800°F (427°C). Total coating thickness (both sides) was about 0.1 mil (0.003mm).
  • the method provides an effective means for removing portions of the base coating to substantially expose a predetermined line pattern of the underlying steel.
  • a subsequent treatment activity on the substantially exposed steel can result in domain refinement and reduced core loss.
  • the flux printing and phosphorus striping method treatment provides excellent heat resistant domain refinement, reduced core loss and retained high magnetic permeability.
  • Figures 4A and 4B are representative photomicrographs 50X and 100X respectively, of the surface of a 7 mil (0.1778mm) test specimen after printing, heating, and phosphorus striping showing iron phosphide particles in the metal stripes.
  • the # 51 flux was used for the 8 mil (0.203mm) samples.
  • the 7 mil (0.1778mm) samples had a somewhat thicker base glass i.e. forsterite, and the following more aggressive modified flux agent was used, designed empirically from a series of test flux firings.
  • Flux No. SSA Phosphoric acid (85%) 27 % wt. Potassium fluoborate 24 % Petroleum jelly 23 %
  • Example 1 Stencilling followed the practice of Example 1 and the flux-printed samples were then fired at approximately 1300°F (704°C).
  • phosphorus striping was by P coating in conjunction with a 5 hour hydrogen diffusion anneal at approximately 1650°F (899°C).
  • Samples of high permeability oriented steel of Steel 2 were flux-printed continuously on a Matthews Model 6029 printing press which is capable of printing on 3 inch (76.2 mm) wide strip material.
  • the press was operated in a flexographic mode (see Figure 2), i.e. the print roll printed directly on the Epstein strips rather than through the action of a blanket roll.
  • the ink base used was Matthews commercial #M165 black ink marketed for conventional printing. It is of syrupy consistency with a viscosity of about 10,000 centipoise (10 Pa.s) To the ink base was added 20% phosphoric acid, by weight.
  • the magnetic core loss properties showed a mild improvement using the diluted fluxing agent-ink composition used for the continuous printing.
  • Example 3 This series of tests on Steel 2 was similar to that in Example 3 except that a much more concentrated fluxing ink was used.
  • the ink was devised by mixing phosphoric acid (85% strength) with poly-ethylene glycol as a thickening agent until viscosity similar to the #M165 commercial black ink used in Example 3 was attained.
  • the fluxing ink contained 75% phosphoric acid and 25% poly-ethylene glycol.
  • This ink printed well and yielded lines of about .025mm (0.1 mil) thickness applied to the forsterite. Line spacing was 5mm and line width 0.25mm. Processing, except for the different ink, was identical to Example 3. Results of tests on eight Epstein strips of 9 mil (0.2286mm) high-permeability oriented steel of Steel 2 are shown below.
  • Example 4 clearly establishes the heat resistant domain refinement possible following the step of using the flux agent to remove portions of the forsterite in a predetermined pattern.
  • the magnetic improvement in core loss was excellent and permanent after SRA for 1 hour at 1475°F (801°C) as shown below: Permeability Core Loss WPP(WKg) @ 10 Oe 1.5T 1.7T MT20 1917 .358 (.789) .484 (1.067) 21 1873 .407 (.897) .584 (1.289) 22 1916 .370 (.816) .536 (1.182) 23 1920 .358 (.789) .506 (1.115) 24 1934 .377 (.831) .555 (1.223) 25 1926 .429 (.946) .585 (1.290) 26 1893 .485 (1.069) .680 (1.499) 27 1938 .367 (.809) .507 (1.118) Average 1915 .394 (.869) .555 (1.223
  • an intermediate method step has been provided for conveniently and inexpensively removing the base coating of grain oriented silicon steel in desired patterns for refining the magnetic domain wall spacing.
  • the method of removing may be in batch mode or continuously, both of which can be incorporated into continuous mill processing of conventional and high permeability grain oriented silicon steel.
  • Firing of the agent to "burn" the stripes through the forsterite would be a simple low cost process step readily amenable to a continuous strand operation. It appears necessary only to heat the strip to temperature in air atmosphere with no hold time required.

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EP90301541A 1989-03-23 1990-02-14 Verfahren zum bereichsweisen Frischen von orientiertem Siliciumstahl Ceased EP0389096A1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
US327946 1981-12-07
US07/327,946 US4968361A (en) 1989-03-23 1989-03-23 Method of domain refinement of oriented silicon steel by using flux-printing

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EP0389096A1 true EP0389096A1 (de) 1990-09-26

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US (1) US4968361A (de)
EP (1) EP0389096A1 (de)
JP (1) JPH0336213A (de)
KR (1) KR900014608A (de)
BR (1) BR9001356A (de)
CA (1) CA2011106A1 (de)
MX (1) MX174014B (de)

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DE19805886C2 (de) * 1998-02-13 2001-07-05 Kuehnhackl Gmbh Verfahren zum Herstellen von keramischen Produkten mit reliefartigen Oberflächen-Strukturen und dabei zu verwendendes lithographisches Abziehbild

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US5078811A (en) * 1989-09-29 1992-01-07 Allegheny Ludlum Corporation Method for magnetic domain refining of oriented silicon steel
US6231924B1 (en) * 1996-11-26 2001-05-15 Nippon Sheet Glass Company, Limited Method of partially forming oxide layer
US6406639B2 (en) 1996-11-26 2002-06-18 Nippon Sheet Glass Co., Ltd. Method of partially forming oxide layer on glass substrate
DE60306365T3 (de) * 2002-05-08 2014-03-13 Ak Steel Properties, Inc. Verfahren zum kontinuierlichen giessen von nichtorientiertem elektrostahlband
US20050000596A1 (en) * 2003-05-14 2005-01-06 Ak Properties Inc. Method for production of non-oriented electrical steel strip
CN101333619B (zh) * 2007-06-25 2010-10-13 宝山钢铁股份有限公司 一种控制取向硅钢二次再结晶晶粒尺寸的工艺方法

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DE2640213A1 (de) * 1975-09-08 1977-03-31 Allegheny Ludlum Ind Inc Verfahren zur herstellung von elektromagnetischem siliciumstahl
DE2247269C3 (de) * 1971-09-27 1981-05-14 Nippon Steel Corp., Tokyo Verfahren zur Herstellung einer isolierenden sowie die Magnetostriktions-Charakteristika und den Eisenverlust verbessernden Schicht auf einem Silicimstahlblech
US4513597A (en) * 1981-09-30 1985-04-30 Nippon Steel Corporation Apparatus for reducing the watt loss of a grain-oriented electromagnetic steel sheet
EP0294134A2 (de) * 1987-06-03 1988-12-07 Allegheny Ludlum Corporation Verfahren zum Herstellen duktiler, hochpermeabler kornorientierter Siliciumstähle

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US4032366A (en) * 1975-05-23 1977-06-28 Allegheny Ludlum Industries, Inc. Grain-oriented silicon steel and processing therefor
US4655854A (en) * 1983-10-27 1987-04-07 Kawasaki Steel Corporation Grain-oriented silicon steel sheet having a low iron loss free from deterioration due to stress-relief annealing and a method of producing the same
JPS6196036A (ja) * 1984-10-15 1986-05-14 Nippon Steel Corp 低鉄損方向性電磁鋼板及びその製造法

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DE2247269C3 (de) * 1971-09-27 1981-05-14 Nippon Steel Corp., Tokyo Verfahren zur Herstellung einer isolierenden sowie die Magnetostriktions-Charakteristika und den Eisenverlust verbessernden Schicht auf einem Silicimstahlblech
US3990923A (en) * 1974-04-25 1976-11-09 Nippon Steel Corporation Method of producing grain oriented electromagnetic steel sheet
DE2640213A1 (de) * 1975-09-08 1977-03-31 Allegheny Ludlum Ind Inc Verfahren zur herstellung von elektromagnetischem siliciumstahl
US4513597A (en) * 1981-09-30 1985-04-30 Nippon Steel Corporation Apparatus for reducing the watt loss of a grain-oriented electromagnetic steel sheet
EP0294134A2 (de) * 1987-06-03 1988-12-07 Allegheny Ludlum Corporation Verfahren zum Herstellen duktiler, hochpermeabler kornorientierter Siliciumstähle

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE19805886C2 (de) * 1998-02-13 2001-07-05 Kuehnhackl Gmbh Verfahren zum Herstellen von keramischen Produkten mit reliefartigen Oberflächen-Strukturen und dabei zu verwendendes lithographisches Abziehbild

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KR900014608A (ko) 1990-10-24
US4968361A (en) 1990-11-06
CA2011106A1 (en) 1990-09-23
BR9001356A (pt) 1991-04-02
JPH0336213A (ja) 1991-02-15
MX174014B (es) 1994-04-14

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